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WO1994005824A1 - Element porteur et son procede de production - Google Patents

Element porteur et son procede de production Download PDF

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Publication number
WO1994005824A1
WO1994005824A1 PCT/JP1993/001137 JP9301137W WO9405824A1 WO 1994005824 A1 WO1994005824 A1 WO 1994005824A1 JP 9301137 W JP9301137 W JP 9301137W WO 9405824 A1 WO9405824 A1 WO 9405824A1
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WO
WIPO (PCT)
Prior art keywords
less
temperature
treatment
structural member
solution
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP1993/001137
Other languages
English (en)
Japanese (ja)
Inventor
Akitsugu Fujita
Takayuki Kawano
Makoto Nakamura
Fumikazu Saika
Tatsuki Matsumoto
Shinsuke Oba
Hidetoshi Sueoka
Manabu Kimura
Masato Zama
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Zama Kazuko
Mitsubishi Heavy Industries Ltd
Original Assignee
Zama Kazuko
Mitsubishi Heavy Industries Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from JP26315892A external-priority patent/JP2786568B2/ja
Priority claimed from JP02250393A external-priority patent/JP3192799B2/ja
Application filed by Zama Kazuko, Mitsubishi Heavy Industries Ltd filed Critical Zama Kazuko
Priority to US08/232,191 priority Critical patent/US5599408A/en
Priority to EP94908809A priority patent/EP0625586B1/fr
Priority to DE69317265T priority patent/DE69317265T2/de
Priority to DK94908809T priority patent/DK0625586T3/da
Publication of WO1994005824A1 publication Critical patent/WO1994005824A1/fr
Priority to FI942014A priority patent/FI103585B/fi
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/78—Combined heat-treatments not provided for above
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0006—Details, accessories not peculiar to any of the following furnaces
    • C21D9/0025—Supports; Baskets; Containers; Covers
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints

Definitions

  • the present invention relates to a structural member and a method of manufacturing the same, particularly to a hydrofoil of a high-speed passenger boat, offshore oil-related equipment, and other structures that require high strength, high toughness and high corrosion resistance and require welding work.
  • the present invention relates to a member and a manufacturing method thereof.
  • the heat treatment of the above structural members is usually performed by quenching and tempering, and after the welding, re-solution treatment and aging treatment are performed.
  • the welded structural members will be deformed by the residual stress or their own weight during the heat treatment, so it is extremely large to prevent such deformation. Even though it is necessary to have strong restraint. Further, even a structural member that does not undergo welding has much lower toughness than the one provided with the heat treatment method of the present invention.
  • the present invention has been made in view of the above circumstances, and provides a structural member capable of preventing deformation during heat treatment and significantly improving toughness, and a method of manufacturing the same. aimed to .
  • the present invention has the features described in the following items (1) to (15).
  • a hydrofoil consisting of stainless steel having a structure with the e-phase protruding into the base where the remainder substantially consists of the martensite phase A ship characterized by having (3) By weight, carbon: 0.07% or less, silicon: 1% or less, manganese: 1% or less, copper: 2.5 to 5%, nickel: 3 to 5 5%, chromium: 14-: 17 .5%, molybdenum: 0.5% or less, niob: 0.15-0.
  • the second solution treatment is further performed after 730 to 840.
  • a method for manufacturing a component, wherein the second aging treatment is performed in the following manner.
  • carbon 0.07% or less
  • silicon 1% or less
  • manganese 1% or less
  • copper 2.5 to 5%
  • nickel 3 to 5 5%
  • chromium 14 to: 177.5%
  • molybden 0.5% or less
  • niobium 0.15 to 0.
  • the first aging was performed.
  • a structural member that is aged at a temperature of 52 O'C or more and 63 O'C or less a structural member having an arbitrary shape is formed by welding, and then a second solution treatment is performed.
  • a method for producing a structural member comprising cooling to a room temperature in a furnace at a cooling rate of 100 / hour or less.
  • the temperature is further increased at a rate of 100 ° C / hour or less, and the second solution heat treatment is carried out at 730 to 8
  • a second aging treatment is performed at a temperature of at least 520 and at a temperature of at least 630. At a cooling rate of less than 100 hours A method of manufacturing a structural member characterized by cooling to room temperature.
  • carbon 0.07% or less
  • silicon 1% or less
  • manganese 1% or less
  • copper 2.5 to 5%
  • nickel oxide 3 to 5%
  • chromium 14 to 17.5%
  • molybdenum 0.5% or less
  • niobium 0.15 to 0.
  • the first solution treatment was performed on stainless steel consisting essentially of iron, with the balance being 50% and the balance, after the first solution treatment was carried out at 110 to 150, and then the first aging treatment was performed. Aging at a temperature of 52 O'C or more and 63 O'C or less, put the material in a container made of a metal plate, and put it together with the container at a speed of 100 hours or less. The temperature was raised, the second solution treatment was performed at 730 to 84 O'C, and after cooling in the furnace to room temperature at a cooling rate of no more than 100'C, the second solution treatment was performed. 5 2 0
  • a method for producing a structural member comprising: cooling to room temperature at a cooling rate of not more than 100 hours in a furnace.
  • carbon 0.07% or less
  • silicon 1% or less
  • manganese 1% or less
  • copper 2.5 to 5%
  • nickel oxide 3 to 5 5%
  • chromium 14-: 17 .5%
  • molybdenum 0.5% or less
  • niob 0.15-0.
  • the first solution treatment was performed on stainless steel consisting of 45% and the balance substantially consisting of iron in a temperature range of 110 to 150, followed by a first aging treatment.
  • the material is placed in a container made of a plate, and the material is heated together with the container at a rate of 100 hours or less, and a second solution treatment is performed at 730-840 ° C. After that, it is cooled to room temperature at a cooling rate of 100 ° C / hour or less in the furnace, and the second aging treatment is performed at a temperature of 500 ° C or more and 63 ° C or less.
  • a method for producing a structural member characterized in that the structure is cooled to room temperature in a furnace at a cooling rate of 100 hours or less.
  • the first solution treatment was performed on stainless steel consisting of 45% and the balance substantially consisting of iron at 110 1 to 150 0, and then aging treatment.
  • the aging treatment is carried out at 100 to 150 ° C, and then the aging treatment is carried out by cooling to room temperature at a cooling rate of 100 ° C / hour or less in the furnace.
  • a method for producing a structural member characterized in that the method is performed in the following manner, and then cooled to room temperature at a cooling rate of 100 hours or less in a furnace.
  • the first solution heat treatment was performed on stainless steel consisting of 45% and the balance substantially consisting of iron in a temperature range of 110 to 150, followed by aging. Ages from O'C to 63 O'C, and the material is put into a container made of metal plate as a structural member of any shape by welding, and the material is put together with the container. Then, the temperature was raised at a rate of 100 hours or less than Z hours, and the second solution treatment was performed at 110 0 to 150 0 'C, and thereafter In the furnace, it is cooled down to room temperature at a cooling rate of 100 / hour or less, and the aging treatment is carried out at a temperature of 52 O'C or more and 63 O'C or less, and then 100% in the furnace.
  • a method for producing a structural member characterized in that the member is cooled to room temperature at a cooling rate of not more than 0 / hour.
  • the alloy composition targeted by the present invention is as follows.
  • Silicon is a deoxidizing agent and works effectively at 1% or less. If it exceeds 1%, it may cause embrittlement, so it should be 1% or less.
  • Mangan is also a deoxidizer and works effectively at 1% or less. If it exceeds 1%, the toughness is reduced and the martensite at the base is destabilized.
  • Copper is a fine intermetallic compound that is bent out during aging to improve the material strength. If the content is less than 2.5%, the effect is not sufficient, and if the content exceeds 5%, the toughness is reduced, so the content is set to 2.5 to 5%.
  • Nickel Nickel dissolves in the matrix and forms an intermetallic compound with copper. If the nickel content is less than 3%, delta ferrite in the matrix precipitates and reduces toughness and ductility. On the other hand, if the amount is more than 5.5%, residual austenite will be present in the matrix at room temperature, so that sufficient strength will be obtained. Is not obtained. For this reason, the content is set to 3 to 5.5% (chromium): Chrome is an essential element for maintaining corrosion resistance and is a main element of this material. If it is less than 14%, sufficient corrosion resistance cannot be obtained. In addition, if the amount exceeds 17.5%, delta lights will precipitate, so the amount is set to 14 to 17.5%. (Molybden): Molybden is an effective element for pitting corrosion resistance. However, if the amount exceeds 0.5%, embrittlement will be caused, so the amount should be 0.5% or less.
  • Niob has a fine grain size and is effective in improving strength, ductility and toughness. If the content is less than 0.15%, the effect is not sufficient, and if it exceeds 0.45%, a large amount of carbide is crystallized during solidification, so that the ductility and toughness are increased. This leads to a decrease in Therefore, it should be 0.15 to 0,45%.
  • the balance is essentially iron, the basic element of stainless steel.
  • structural member of the present invention described in the above item (1) or (2) further has the following structure in addition to the above composition.
  • the reverse transformation austenite phase occurs in the matrix's martensite phase as an austenite phase.
  • Tenite phase In addition to improving the overall toughness of the matrix by virtue of its properties, the austenite phase also increases the strength of the matrix.
  • the toughness of the martensite can be further improved by the composite effect of making the martensite grains smaller by folding it out into the it phase. If the content is less than 6% by volume, the toughness is not sufficiently improved, and if it exceeds 30%, the strength of the matrix becomes insufficient, so that the austenite phase is 6 to 3%. 0% by volume.
  • the content is preferably 10 to 25% by volume.
  • the first solution treatment and aging treatment are usually heat treatment methods for the material of the present invention, and are specified in JIS G4303 as heat treatment methods for SUS630. It has the same purpose as the original.
  • this heat treatment the solute atoms present in the cell are once dissolved in the matrix by the solution treatment of 110 to 150 ° C, and then added to the microstructure. Rectification (component bias), and then aging treatment in the range of 52 to 63 0 to extract the copper-rich intermetallic compound ( ⁇ phase), resulting in high strength You get the material.
  • the second solution treatment and the aging treatment are particularly important points, and as a result, the material is treated with respect to the material. High toughness and uniform mechanical properties and high toughness are imparted to the weld.
  • the second solution heat treatment temperature is lower than the first solution heat treatment temperature, and by controlling the capping temperature and the cooling rate in the heat treatment. In addition, the deformation of the material due to heat treatment can be suppressed to an extremely low level.
  • welding is carried out after the first solution treatment and aging treatment or after the first solution treatment.At this time, the molten metal part and the heat affected zone are originally applied to this material. Should be heat treated Since the part where nothing is done (the molten metal part) or the heat treatment that has been applied up to that point will be the part where the cancellation is made (the heat affected part), The required strength, toughness, and other properties have been impaired, and heat treatment must be performed again.
  • the second solution treatment is performed.
  • This process is performed at 730-840, but since this process can be performed while maintaining the strength of the material as compared with the normal solution treatment, Even if this heat treatment is applied to a large-sized welded structural member in particular, the amount of deformation is small compared to the first solution treatment, and the product can be easily heat-treated.
  • the above-described solution treatment at a low temperature is employed, and the temperature control during the heat treatment is performed. As a result, the temperature difference between each part of the material is reduced, and the deformation of the material can be extremely reduced.
  • the temperature control method according to the present invention will be described later.
  • the second solution treatment and the second aging treatment can contribute to the material excellent toughness that cannot be obtained by ordinary heat treatment. it can .
  • the as-welded part of the weld has a softened zone in the heat affected zone (HAZ). This is due to the fact that the steel is kept at a high temperature by welding, so that aging proceeds and overage softening occurs (the intermetallic compound proceeds to break out, the deposited material becomes cohesive and coarse, and the strength decreases). Phenomenon). In this case, This member will crack and break from the weakly heat affected zone earlier than its service life. In order to eliminate such a defect, a re-solution treatment is usually performed. In this ordinary re-solution treatment, the temperature is the same as the first solution treatment temperature of the present invention. However, in this case, since the temperature is maintained at a high temperature as described above, the residual stress of welding and the self-treatment may occur. The stresses due to the weights cause deformation and make it difficult to shape the product.
  • the solution heat treatment is performed at a heat treatment temperature considerably lower than the first solution heat treatment temperature.
  • the heat treatment can be performed with less deformation than in the solution treatment of 1.
  • the solution treatment temperature exceeds the Ac 3 transformation temperature (the temperature at which all the transformation from the low-temperature phase martensite phase to the high-temperature phase austenite phase) occurs. Therefore, most of the solute atoms form a solid solution, and an effect equivalent to that of the solution treatment can be obtained.
  • the solution treatment temperature is low, the diffusion of solute atoms dissolved from the precipitate is not sufficient, and micro-bias remains.
  • This micro-bias is rich in copper and nickel, which are the austenite phase-forming elements, so that the average aging of the entire material during post-process aging treatment Austenite transformation occurs at a temperature lower than the A c 1 transformation temperature (called reverse transformation austenite), and contributes to improvement in toughness.
  • the austenite phase has excellent corrosion resistance and Since there is no deterioration in corrosion resistance at the boundary with the tensite phase, there is no problem with use in corrosive environments such as seawater.
  • This second solution treatment temperature is 8
  • the temperature is higher than 40 mm, large structural members undergo significant deformation during heat treatment, so a large restraining jig is required, and the cost of man-hours increases. This will lead to an increase in the number of tops and seasons.
  • the second solution heat treatment temperature was limited to 730 to 840.
  • the martensite structure quenched by the second solution treatment is tempered to form a martensite structure, and the solute atoms dissolved in the solid solution are added. This is done to obtain appropriate strength by extracting it as an intermetallic compound called the e-phase rich in copper and nickel.
  • reverse transformation austenite appears by this heat treatment, and high toughness can be obtained. If the aging treatment temperature exceeds 630, overaging softening occurs, the strength decreases, and the necessary and sufficient strength cannot be obtained. Also,
  • the object of the present invention described in (13) to (15) is to apply a welding process to the material obtained as described above to obtain a desired shape.
  • Deformation in subsequent heat treatment An object of the present invention is to provide a heat treatment method so that the heat treatment can be performed with the least possible amount.
  • a part of the heat-affected zone of welding is maintained at a high temperature, so that the extracted solute atoms are matri- It may form a solid solution in the gauze, or it may break out and cause a drop in strength.
  • the temperature rises from the martensite phase (low temperature phase) to the austenite phase.
  • the following temperature control method is employed in order to prevent such deformation.
  • the reasons for limiting the temperature control method as the second point in the present invention are as follows.
  • the rate of temperature rise and temperature decrease in the solution treatment and the aging treatment so that fuel cost can be saved.
  • it is rapidly heated, and quenching at a relatively high speed such as quenching of water or oil or air cooling is applied.
  • the structural member mainly targeted by the present invention it is often a welded structure, and even if it is not a welded structure, it may be a thin large-sized structure.
  • a heat treatment at a lower temperature than before is selected in order to prevent deformation of the structural member.
  • the rate of temperature rise and fall is specified, and by minimizing the temperature difference between each part of the material as much as possible, deformation of structural members can be prevented.
  • the heat treatment is performed at a high rate, where the temperature of the heating and cooling rate exceeds 100 / hour, the heat treatment is performed even at the second solution heat treatment temperature at which the heating temperature is lower than before.
  • the heating and cooling rates should be 100 ° C / hour or less.
  • the material to be heat-treated when the material to be heat-treated is directly placed in a heating furnace, if the material is large, the material is locally heated by radiant heat from the heating furnace. To prevent localized heating of the material due to radiant heat, the material is wrapped in a metal plate (referred to as “muffle”), and the entire muffle is wrapped. Heating reduces the temperature difference, further preventing material deformation it can .
  • the use of this mask not only can prevent radiant heat during the heating process, but it can also be achieved by local air blown from outside the furnace during cooling. Cooling can also be prevented, and the temperature difference between each part of the material can be extremely small.
  • the temperature is maintained during the temperature rise and fall, so that the temperature difference between the various parts caused by the temperature change up to that point is maintained.
  • the temperature difference is maintained in the heating process.
  • there is an Ac 1 transformation point (the temperature at which the high-temperature austenite phase starts to appear from the low-temperature martensite phase) near 65 O'C.
  • this transformation causes volume shrinkage.
  • the temperature difference is large in each part of the material, a difference appears in the volume change between the transformed part and the non-transformed part, which becomes stress and is added to the material itself. As a result, deformation occurs.
  • the temperature is raised once in the range of 550 to 62 0 below the transformation start temperature, and after the temperature of each part of the material becomes uniform, Try to raise the temperature of the process.
  • the retention temperature is lower than 550, a temperature difference will occur in each part of the material while the temperature rises to the transformation temperature. In some cases, this effect may not be obtained.
  • the temperature is maintained at more than 620, some components of the present invention may exceed the Ac1 transformation point. Therefore, the holding temperature during heating is preferably 550 to 62 O'C. Yes.
  • M s point the temperature at which the high-temperature austenitic phase starts to appear in the low-temperature martensite phase
  • the holding temperature at the time of cooling is preferably from 300 to 220 • C.
  • FIG. 1 is an explanatory view showing a groove shape before welding of a TIG welding test piece employed in an example of the present invention
  • FIG. 2 is a diagram showing a shape of a mat according to an example of the present invention
  • FIG. 3 is a diagram for explaining the amount of deformation of the test piece measured in the example of the present invention
  • FIG. 4 is a photograph of a cross-sectional metal structure by an optical microscope
  • FIG. 5 is an optical microscope.
  • Cross-sectional metallographic photograph by The figure is a schematic view of the structure of the hydrofoil ship
  • FIG. 7 is a front view of the hydrofoil ship
  • FIG. 8 is a perspective view of the bow wing
  • FIG. 9 is a perspective view of the stern wing.
  • test materials were melted in a 25-ton electric furnace with the components shown in Table 1 below, refined in a 30-ton ladle refining furnace, and used as an electrode for secondary melting by the bottom pouring method. Then, it was remelted in an electroslag remelting furnace (ESR furnace) to obtain a forging material. After that, it was forged into a plate material having a thickness of 65 mm and subjected to the test.
  • ESR furnace electroslag remelting furnace
  • this material 1 was processed into the shape shown in Fig. 1 and subjected to TIG welding under the welding conditions shown in Table 3 below to obtain a welded joint.
  • O, ⁇ , LI in Fig. 1 Is 6 5 mm, L
  • the heating and cooling rates in the second solution treatment and aging should be about 50 hours.
  • the material was subjected to the same heat treatment and welding as described above, while controlling the target. A mechanical test similar to the above was performed on the member obtained in this manner. The results are shown in Table 7 below.
  • this material was formed into a plate with a length of 3 m, a width of 50 cm and a thickness of 6 Omm, : 5 m 80 cm, Height: 4 m, Depth: 25 m Charged into an oil-fired heating furnace, subjected to a second solution treatment and a second aging treatment, and the material before and after heat treatment The amount of deformation was measured. The measurement results are shown in Table 8 below. It should be noted that, in this table, "Matsunore" means a container made of a metal plate. In this experiment, as shown in Fig.
  • a mats 2 made of JISSUS304 Stainless Steel and having a length and width of 2 m and a length of 15 m was used.
  • the test material 1 was fixed with a base 4 provided between the jigs and a jig 3 for holding the test material on both sides.
  • the test material was 3 m in length, 600 mm in width and 50 mm in thickness.
  • the amount of deformation was before the second solution treatment and aging treatment in the thickness direction.
  • the amount of displacement ⁇ ? From 1a to 1b after processing was measured (see Fig. 3). The measurement results are shown in Table 8 below.
  • TIG welding was performed on the material under the same welding conditions as in Table 3 above. Further, this welded plate material was cut out to the same dimensions as above, put into the above-mentioned muffle, and charged into the above-mentioned oil-fired heating furnace, and then heated at 790 ° C for 3 hours. A second solution treatment of time was performed and a second aging treatment of 570 ° C. for 4 hours was performed. In addition, the heating and cooling rates of this heat treatment were controlled at 50 ° C for the target time, and the cooling after the second solution treatment was performed in order to make sure (B) Processing was performed.
  • This passenger boat is provided with wings 16 at the front and rear of the hull 11 via wing columns 17 respectively.
  • the hull 11 is provided with a water pipe 20 communicating with the stern-side wing support 17, and a port-type suction port 15 is provided at the inlet end of the water pipe 20 of the wing support 17.
  • a hull 11 is provided with a jet nozzle 21 at a side end thereof. The water flow is accelerated by a pump 12 provided in a water pipe 20, and the pump 12 is driven by a propulsion unit Min 13.
  • this embodiment is of a catamaran type, and two wing supports 17 are provided at each of the front and rear portions of the ship. A pair of these wing supports 17 are provided.
  • the wing 16 is fixed.
  • Figures 8 and 9 show enlarged views of the wing 16 and wing column 17 on the bow and stern sides.
  • the cross-sectional shape of the wing 16 and the wing 16 and the wing column 17 are almost lens-shaped or streamlined.
  • the rear part of the wing column 17 on the bow side is a rudder flap 18, which allows the high-speed passenger boat to turn left and right by panning left and right. .
  • the rear portions of the front and rear wings 16 are flaps 19, respectively, and control the high-speed passenger boat up and down by rotating up and down.
  • a structural member manufactured by the same method as in Experiment 5 is used as the wing 16 described above.
  • the structure obtained by this method Since the member is prevented from being deformed during the heat treatment and is easily tough, the use of the member as the wing 16 gives the following advantages to the high-speed passenger boat.
  • Fluid resistance increases if the wing shape, which reduces fluid resistance as much as possible by design, becomes non-uniform, but using the wing of the present invention reduces fluid resistance.
  • the propulsion efficiency can be improved.
  • the welded joint was subjected to the second solution treatment (3 hours) and the aging treatment (4 hours) shown in Table 11 below, and an accuracy test was performed.
  • the test results are shown in Table 11 below.
  • the heat-treated material used here was subjected to a heat treatment by increasing and decreasing the temperature at a rate of 50 hours. As is clear from these results, it is understood that the test material subjected to the heat treatment method of the present invention shows the same mechanical properties as the material. 11
  • the impact test of the weld was performed with a notch in the heat-affected zone.
  • the above-mentioned material is formed into a plate of length: 3 m, width: 50 cm, plate: 60 mm, frontage: 5 m, 80 cm,
  • the sample was placed in an oil-fired heating furnace with a height of 4 m and a depth of 25 m, subjected to a second solution treatment and aging treatment, and the deformation of the material before and after the heat treatment was measured.
  • the measurement results are shown in Table 12 below.
  • the mask in this table is a container made of a metal plate as described above, and an example is shown in Fig. 2.
  • 1 is the test material (length: 3 m, width: 50 cm, plate thickness: 60 mm)
  • 2 is the JISSUS304 mattress
  • 3 is the test material holding
  • the jig, 4 is a base.
  • the structural member and its manufacturing method of the present invention it is possible to perform a heat treatment after welding of a large welded structural member that cannot be performed by a conventional heat treatment method.
  • the hardness distribution of the weld after heat treatment is uniform, and in addition, it is possible to have excellent toughness that cannot be obtained by conventional heat utilization methods.
  • the deformation of the material during heat treatment can be extremely reduced.

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  • Heat Treatment Of Steel (AREA)

Abstract

L'invention concerne un élément porteur qui se compose en poids de 0,07 % de carbone au plus, 1 % de silicium au plus, 1 % de manganèse au plus, 2,5 % à 5 % de cuivre, 3 à 3,5 % de nickel, 14 à 17,5 % de chrome, 0,5 % de molybdène au plus, 0,15 à 0,45 % de niobium, le solde étant pour l'essentiel constitué de fer, élément porteur pour lequel on dépose une phase ε dans une matrice composée de 6 à 30 % en volume d'une phase austénitique, le reste consistant pour l'essentiel en une phase martensitique. L'invention concerne également un procédé qui permet de produire cet élément porteur en soumettant un acier inoxydable présentant la composition mentionnée à un premier recuit d'homogénéisation au stade solidus entre 1010 et 1050 °C, puis à un vieillissement entre 520 et 630 °C, et à un deuxième recuit d'homogénéisation au stade solidus entre 730 et 840 °C avant un vieillissement entre 520 et 630 °C. On peut aussi procéder à un soudage destiné à conférer à l'élément porteur une forme voulue avant le deuxième recuit d'homogénéisation au stade solidus. Un autre procédé qui permet de produire un élément porteur consiste à soumettre un acier inoxydable présentant la composition mentionnée au premier recuit d'homogénéisation au stade solidus entre 1010 et 1050 °C puis au vieillissement entre 520 et 630 °C, à effectuer un soudage pour lui conférer une forme voulue, à élever la température au rythme de 100 °C/h au moins, à procéder au deuxième recuit d'homogénéisation au stade solidus entre 1010 et 1050 °C, à abaisser la température du four à la température ambiante à un rythme de refroidissement de 100 °C/h ou moins, à procéder au vieillissement entre 520 et 630 °C, et à abaisser la température du four à la température ambiante à un rythme de refroidissement de 100 °C/h ou moins.
PCT/JP1993/001137 1992-09-04 1993-08-12 Element porteur et son procede de production Ceased WO1994005824A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
US08/232,191 US5599408A (en) 1992-09-04 1993-08-12 Method of producing a structural member
EP94908809A EP0625586B1 (fr) 1992-09-04 1993-08-12 Element porteur et son procede de production
DE69317265T DE69317265T2 (de) 1992-09-04 1993-08-12 Konstruktionselement und dessen herstellung
DK94908809T DK0625586T3 (da) 1992-09-04 1993-08-12 Konstruktionselement og fremgangsmåde til fremstilling af dette
FI942014A FI103585B (fi) 1992-09-04 1994-04-29 Rakenneosa ja sen valmistusmenetelmä

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP4/263158 1992-09-04
JP26315892A JP2786568B2 (ja) 1992-02-14 1992-09-04 構造部材とその製法
JP5/22503 1993-02-10
JP02250393A JP3192799B2 (ja) 1993-02-10 1993-02-10 構造部材の製造方法

Publications (1)

Publication Number Publication Date
WO1994005824A1 true WO1994005824A1 (fr) 1994-03-17

Family

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Application Number Title Priority Date Filing Date
PCT/JP1993/001137 Ceased WO1994005824A1 (fr) 1992-09-04 1993-08-12 Element porteur et son procede de production

Country Status (7)

Country Link
US (1) US5599408A (fr)
EP (1) EP0625586B1 (fr)
KR (1) KR0149740B1 (fr)
DE (1) DE69317265T2 (fr)
DK (1) DK0625586T3 (fr)
FI (1) FI103585B (fr)
WO (1) WO1994005824A1 (fr)

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US6245289B1 (en) 1996-04-24 2001-06-12 J & L Fiber Services, Inc. Stainless steel alloy for pulp refiner plate
US5877428A (en) * 1997-05-29 1999-03-02 Caterpillar Inc. Apparatus and method for measuring elastomeric properties of a specimen during a test procedure
US6550122B1 (en) * 1999-10-22 2003-04-22 Honda Giken Kogyo Kabushiki Kaisha Method of manufacturing laminated ring
KR100821117B1 (ko) * 2001-06-29 2008-04-11 에드워드 제이. 맥크링크 스틸 구조물 및 그 형성 방법
US6743305B2 (en) * 2001-10-23 2004-06-01 General Electric Company High-strength high-toughness precipitation-hardened steel
US20060196853A1 (en) * 2005-03-04 2006-09-07 The Regents Of The University Of California Micro-joining using electron beams
GB2424422A (en) * 2005-03-23 2006-09-27 Alstom Technology Ltd Precipitation hardening of a steel
WO2007108058A1 (fr) * 2006-03-16 2007-09-27 Mole's Act Co., Ltd. Procede de liaison d'elements en acier, procede de renforcement de la force de liaison d'un objet unifie comprenant des elements en acier, produit en acier, et produit coule sous pression
US7854809B2 (en) 2007-04-10 2010-12-21 Siemens Energy, Inc. Heat treatment system for a composite turbine engine component
CN102251084B (zh) * 2011-07-04 2013-04-17 南京迪威尔高端制造股份有限公司 深海采油设备液压缸用钢锻件性能热处理工艺
CN107970580A (zh) * 2016-10-19 2018-05-01 复盛应用科技股份有限公司 高尔夫球杆头的制造方法
KR20180104513A (ko) * 2017-03-13 2018-09-21 엘지전자 주식회사 공기 조화기
RU2691022C1 (ru) * 2018-03-28 2019-06-07 Общество с ограниченной ответственностью "Производственное коммерческое объединение "Термическая обработка металлов" Способ поверхностной термообработки изделий из нержавеющих хромистых сталей
CN111793741B (zh) * 2019-08-09 2021-08-17 中南大学 一种调控时效硬化合金析出相分布及尺寸的热处理方法
JP2023122798A (ja) * 2022-02-24 2023-09-05 株式会社プロテリアル マルテンサイト系析出硬化型ステンレス鋼の製造方法およびマルテンサイト系析出硬化型ステンレス鋼製品

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Also Published As

Publication number Publication date
FI103585B1 (fi) 1999-07-30
EP0625586A4 (fr) 1995-01-11
DE69317265T2 (de) 1998-07-09
DK0625586T3 (da) 1998-09-28
DE69317265D1 (de) 1998-04-09
FI942014A7 (fi) 1994-04-29
US5599408A (en) 1997-02-04
EP0625586B1 (fr) 1998-03-04
FI103585B (fi) 1999-07-30
FI942014A0 (fi) 1994-04-29
EP0625586A1 (fr) 1994-11-23
KR0149740B1 (ko) 1998-11-16

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